MgB2—based superconductor with high critical current density, and method for manufacturing the same

The present invention relates to an MgB2-based superconductor that is easy to manufacture and well suited to mass production, and that exhibits excellent superconducting characteristics (such as a high critical current density) while still retaining the high critical temperature characteristics of MgB2. A powder mixture of magnesium, boron, and titanium is pressed into a pellet, and this product is sintered under an atmospheric pressure and other conditions (preferably at 600° C. or higher) to manufacture an MgB2-based superconductor in which titanium and/or a titanium compound are dispersed in polycrystalline MgB2. The composition of the MgB2-based superconductor is preferably adjusted to have an atomic ratio of Mg:B:Ti=x:2:y, 0.7<x<1.2 and 0.05<y<0.3, and more preferably 0.07<y<0.2, by adjusting the amounts in which the raw materials are added.

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Description
TECHNICAL FIELD

This invention relates to a MgB2-based superconductor that has excellent superconducting characteristics, such as exhibiting a high critical current density, etc., and is easy to manufacture, and to a method for manufacturing this superconductor.

BACKGROUND ART

Metal-based superconductor materials such as NbTi and Nb3Sn are the most common materials today for superconductor wires used in strong magnetic field magnets and so forth. However, because these materials have a very low critical temperature Tc, the temperature at which they can be used is limited to the temperature range of liquid helium, and therefore there has been a big problem associated with quenching the superconductors.

In light of this, there has recently been considerable interest in reports pertaining to the superconductor characteristics of MgB2, which is a boride of magnesium, and the utility of MgB2 as a superconductor material has been examined from various angles.

MgB2 is advantageous in terms of quenching because its critical temperature Tc is a relatively high 39K, and the usable temperature is expected to be expanded to 20K, which is higher than that attainable with conventional intermetallic compound superconductors. However, in order to obtain it as a material that exhibits a high critical current density, the material has to be synthesized in a high-pressure atmosphere (such as 40,000 to 60,000 atm) and, therefore, it holds little promise for application as a superconductor material which now needs to be mass produced at a low cost.

An example of articles disclosing the above prior art is that of Y. Takano, H. Takeya, H. Fuji, H. Kumakujira, T. Hatano, K. Togano, H. Kito, and H. Ihara, Appl. Phys. Lett., 78, 2914 (2001).

DISCLOSURE OF THE INVENTION

In light of the above situation, it is an object of the present invention to provide an MgB2-based superconductor that is easy to manufacture and well suited to mass production, and exhibits a high critical current density while still retaining the high critical temperature characteristics of MgB2.

As a result of diligent research aimed at achieving the stated object, the inventors arrived at the finding that although sintering must be performed in a high-pressure atmosphere (40,000 to 60,000 atm) in order to obtain a polycrystalline MgB2 sintered body that exhibits a high critical current density with a conventional method in which a mixed powder of magnesium and boron is used as a sintering powder, if a suitable amount of metallic titanium is added as a sintering aid to magnesium and boron, and the resulting mixed powder is used as the sintering powder, then it is possible to stably obtain a polycrystalline MgB2-based superconductor that exhibits a high critical current density while still retaining its high critical temperature characteristics, even if the sintering is performed in an atmosphere equivalent to an atmospheric pressure.

The present invention was made on the basis of the finding and others, and provides a MgB2-based superconductor and a method for manufacturing the same, as described in (1) to (11) below.

(1) An MgB2-based superconductor with high critical current density, wherein either titanium or a titanium compound or both thereof is dispersed in an MgB2-based sintered body.

(2) The MgB2-based superconductor with high critical current density according to (1) above, wherein either the titanium or the titanium compound or both thereof is present at the MgB2 crystal grain boundary.

(3) The MgB2-based superconductor with high critical current density according to (1) or (2) above, wherein when the amounts of magnesium, boron, and titanium contained in the sintered body are expressed as an atomic ratio of Mg:B:Ti=x:2:y, x and y are such that 0.7<x<1.2 and 0.05<y<0.3.

(4) The MgB2-based superconductor with high critical current density according to (1) or (2) above, wherein when the amounts of magnesium, boron, and titanium contained in the sintered body are expressed as an atomic ratio of Mg:B:Ti=x:2:y, x and y are such that 0.7<x<1.2 and 0.07<y<0.2.

(5) The MgB2-based superconductor with high critical current density according to any of (1) to (4) above, wherein the superconductor has a critical current density of at least 5×105 A/cm2 at a temperature of 20K and in a self field.

(6) The MgB2-based superconductor with high critical current density according to any of (1) to (4) above, wherein the superconductor has a critical current density of at least 2×105 A/cm2 at a temperature of 20K and in a magnetic field of 1 T.

(7) A method for manufacturing the MgB2-based superconductor with high critical current density according to any of (1) to (6) above, the method comprising compacting a mixture of magnesium, boron, and titanium and sintering the pressed mixture.

(8) A method for manufacturing the MgB2-based superconductor with high critical current density according to any of (1) to (6) above, the method comprising forming a mixture of magnesium, boron, and titanium into a wire and firing the wire.

(9) A method for manufacturing the MgB2-based superconductor with high critical current density according to any of (1) to (6) above, the method comprising sintering a mixture of magnesium, boron, and titanium, pulverizing the sintered mixture to powder, forming the powder into a wire and firing the wire.

(10) The method for manufacturing the MgB2-based superconductor with high critical current density according to any of (7) to (9) above, wherein the sintering is performed under an atmospheric pressure.

(11) The method for manufacturing the MgB2-based superconductor with high critical current density according to any of (7) to (10) above, wherein the sintering is performed at a temperature of at least 600° C.

The MgB2-based superconductor of the present invention and the method for manufacturing this superconductor will now be described in specific terms.

According to the manufacturing method of the present invention, a mixture of magnesium, boron, and titanium is pressed into pellets and sintered (fired). Thus, there can be obtained a dense MgB2-based superconductor in which either titanium or a titanium compound or both thereof is dispersed.

FIG. 1 is a schematic diagram illustrating an example of the method for manufacturing the MgB2-based superconductor according to the present invention.

A superconductor bulk material is generally obtained by sintering, while a superconductor wire is obtained by firing, but in this Specification the terms sintering and firing are used interchangeably.

To press the mixture of magnesium, boron, and titanium, a standard pressure of about 50 to 200 MPa should be applied in the manufacture of the sintered body.

When a wire is to be manufactured, the above-mentioned mixture is packed into a metal pipe to form it into a wire, which is then fired. In this case, it is also possible to pulverize a sintered body of a mixture of magnesium, boron, and titanium, and pack the sintered powder thus obtained into a metal pipe to form it into a wire.

The sintering may be conducted at any temperature at which a reaction producing an MgB2-based sintered body (superconductor) will occur, but since the reaction of magnesium (melting point: 650° C.) is accelerated at a temperature of 600° C. or higher, it is preferable that the sintering temperature be at least 600° C. but also be such that the magnesium will not evaporate away.

It is good for the atmosphere during sintering to be a non-oxidative atmosphere (such as an inert gas atmosphere), and from the standpoints of cost and the characteristics of the MgB2-based superconductor obtained, the use of an argon gas atmosphere is recommended.

An atmospheric pressure (an atmosphere pressure equivalent to an atmospheric pressure) is sufficient during sintering, but of course there is no harm if the sintering is performed under high-pressure.

The above-mentioned “MgB2-based superconductor in which either titanium or a titanium compound or both thereof is dispersed” obtained by the manufacturing method of the present invention also encompasses a case in which either titanium or a titanium compound or both thereof is dispersed mostly at the grain boundary of polycrystalline MgB2, but some is also present within the crystal grains.

Because either titanium or a titanium compound or both thereof is dispersed in this polycrystalline MgB2, the MgB2-based superconductor is extremely dense even when sintered at an atmospheric pressure.

With this MgB2-based superconductor, it has been found that the superconducting critical temperature Tc thereof is close to 39K, and the critical current density at a temperature of 20K and in a self-magnetic field is 5×105 A/cm2 or higher, and reaches 2×105 A/cm2 or higher at a temperature of 20K and in a magnetic field of 1 T (with respect to this material, when the amounts of magnesium, boron, and titanium in the MgB2-based superconductor obtained in the examples given below are expressed as an atomic ratio of Mg:B:Ti=x:2:y, the value of x is 0.9 and the value of y is 0.1).

The above-mentioned MgB2-based superconductor obtained by the manufacturing method of the present invention is characterized in that its irreversibility field Hirr is closer to an upper critical field Hc2 than when no titanium is contained.

In general, a superconductor will maintain its superconducting state below the upper critical field Hc2, but above the irreversibility field Hirr, the magnetic flux within the superconductor moves, generating resistance, so superconductive current is unable to flow. In other words, if the irreversibility field Hirr is close to the upper critical field Hc2, a large superconducting current can flow even if a high magnetic field is applied, so it is preferable for the irreversibility field Hirr to be close to the upper critical field Hc2, and in this respect the above-mentioned MgB2-based superconductor containing titanium can be considered a preferable material.

The above-mentioned MgB2-based superconductor obtained by the manufacturing method of the present invention is extremely dense because of the titanium and/or titanium compound dispersed therein, even though it is a polycrystalline MgB2 sintered body produced at an atmospheric pressure. This major reason is believed to be that the high critical current density and so forth desired in a superconductor material are exhibited. (Incidentally, when the sintering is performed at an atmospheric pressure without any titanium being added, the resultant sintered body is generally porous and has low density, and the critical current density is also markedly inferior.)

In some cases, the titanium compound present in the polycrystalline MgB2 is TiB2, TiB4, or the like, which are compounds produced during sintering from the titanium added to the raw material mixture, and it seems that these compounds, like titanium, can serve as a pinning center that stops the movement of the lines of magnetic flux without significantly affecting the critical temperature of the MgB2 sintered body, and provide higher critical current density and so on.

In the MgB2-based superconductor according to the present invention, it is preferable for the composition thereof to be adjusted so that when the amounts of magnesium, boron, and titanium are expressed as an atomic ratio of Mg:B:Ti=x:2:y, x and y are within the ranges of 0.7<x<1.2 and 0.05<y<0.3. Adjusting the composition to within these ranges realizes the provision of a superconductor with even better superconducting characteristics (such as critical current density, intensity of magnetization, and irreversibility field). Preferably, if the above-mentioned titanium content y is adjusted to a range of 0.07<y<0.2, the superconducting characteristics will stabilize at an even better level.

The compositional adjustment of the MgB2-based superconductor can be made by adjusting the mixing amounts of the respective raw materials of magnesium, boron, and titanium at the stage of preparing the raw materials.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic diagram illustrating an example of the method for manufacturing the MgB2-based superconductor according to the present invention.

FIG. 2 is a schematic diagram illustrating the treatment steps entailed by the manufacture of an MgB2-based superconductor in examples.

FIG. 3 is a transmission electron micrograph of an MgB2-based superconductor obtained in the examples (x=0.9 and y=0.1 in an atomic ratio of Mg:B:Ti=x:2:y).

FIG. 4 is a graph of the results of measuring the temperature dependence of magnetic susceptibility in MgB2-based superconductors obtained in the examples (when x=1 and y=0, when x=0.9 and y=0.1, when x=0.8 and y=0.2, and when x=0.6 and y=0.4 in an atomic ratio of Mg:B:Ti=x:2:y).

FIG. 5 is a graph of the relationship between the titanium content of an MgB2-based superconductor obtained in the examples (the value of y in an atomic ratio of Mg:B:Ti=x:2:y), the magnetic susceptibility M, and the critical temperature Tc.

FIG. 6 is a graph of the magnetic field dependence of the critical current density Jc at various temperatures for MgB2-based superconductors obtained in the examples (when x=0.9 and y=0.1, when x=0.8 and y=0.2, and when x=1 and y=0 in an atomic ratio of Mg:B:Ti=x:2:y).

FIG. 7 is a graph of the temperature dependence of the irreversibility field Hirr and the upper critical field Hc2 for each MgB2-based superconductor obtained in the examples (when x=0.9 and y=0.1, when x=0.8 and y=0.2, and when x=1 and y=0 in an atomic ratio of Mg:B:Ti=x:2:y).

 BEST MODE FOR CARRYING OUT THE INVENTION

As discussed above, the present invention provides an MgB2-based superconductor with excellent superconducting characteristics, without requiring sintering in a high-pressure atmosphere. The present invention will now be described in more specific terms through examples.

EXAMPLE 1

Magnesium powder, boron powder (amorphous), and titanium powder, each having a purity of 99% and a particle size passing through a 300 mesh sieve, were mixed at an atmospheric pressure and pressed into a pellet (green compact) 7 mm in diameter and 6 mm high.

This pellet (green compact) was then placed on an MgO plate inside an electric furnace, and heated first for 1 hour at 600° C. and then for 1 hour at 800° C. in a 1 atm argon gas flow, after which this product was heated for 2 hours at 900° C., and then cooled to room temperature inside the electric furnace. This treatment yielded MgB2-based superconductors (sintered bodies).

FIG. 2 is a schematic diagram illustrating the treatment steps in this example.

The amounts in which the raw material powders were supplied were adjusted so as to obtain MgB2-based superconductors with various different titanium contents, where the x and y values (x, y) were (1, 0), (0.98, 0.02), (0.95, 0.05), (0.9, 0.1), (0.8, 0.2), (0.6, 0.4), (0.2, 0.8), and (0, 1) when the amounts of magnesium, boron, and titanium were expressed by an atomic ratio of Mg:B:Ti=x:2:y.

The crystallinity of each sample thus produced was evaluated by XRD (X-ray diffraction) and HRTEM (high resolution transmission electron microscope) equipped with EDS (energy dispersion spectroscopy), and as a result it was found that the amount (volume fraction) of superconducting phase was the largest at x=0.9 and y=0.1.

FIG. 3 is an HRTEM photograph (transmission electron micrograph) of the MgB2-based superconductor obtained by adding titanium (x=0.9 and y=0.1 in an atomic ratio of Mg:B:Ti=x:2:y).

In FIG. 3, the portion that appears black is the dispersed titanium phase, while the other portion that appears brighter is the MgB2 crystal phase.

Next, the superconducting characteristics were tested for the various MgB2-based superconductors obtained above.

First, FIG. 4 is a graph of the results of measuring the temperature dependence of magnetic susceptibility (cooling in a zero magnetic field) in the obtained MgB2-based superconductors (when x=1 and y=0, when x=0.9 and y=0.1, when x=0.8 and y=0.2, and when x=0.6 and y=0.4), and it can be seen that all of the superconductors exhibited a high critical temperature Tc value between 37.5 and 38.6K.

FIG. 5 is a graph of the results of examining the titanium atomic ratio (y), the magnetic susceptibility M, and the critical temperature Tc. It can be seen that when the value of y is within the range of 0.05<y<0.3, a high magnetization is exhibited without any substantial adverse effect on the critical temperature Tc.

FIG. 6 is a graph of the magnetic field dependence of the critical current density Jc at various temperatures for the obtained MgB2-based superconductors (when x=0.9 and y=0.1, when x=0.8 and y=0.2, and when x=1 and y=0). It can be seen that compared to a material in which y=0 (a material containing no titanium), a material in which x=0.9 and y=0.1 and a material in which x=0.8 and y=0.2 exhibit far higher critical current density Jc values.

Table 1 is a compilation of the results of measuring the critical current density Jc at various temperatures and magnetic fields for the MgB2-based superconductors obtained in the examples (when x=0.9 and y=0.1).

TABLE 1 Results of measuring critical current density Critical current Temperature (K) Magnetic field (T) density (A/cm2) 5 0   2 × 106 5 2   3 × 105 5 5   5 × 104 20 0 1.3 × 106 20 1 3.1 × 105 20 2 9.4 × 104 20 3 1.7 × 104 35 0 1.2 × 105

FIG. 7 is a graph of the temperature dependence of the irreversibility field Hirr and the upper critical field Hc2 for MgB2-based superconductors obtained in the examples (when x=0.9 and y=0.1, when x=0.8 and y=0.2, and when x=1 and y=0). It can be seen that compared to a material in which y=0 (a material containing no titanium), a material in which y=0.1 or y=0.2 exhibits an irreversibility field Hirr that is closer to the upper critical field Hc2.

Therefore, the MgB2-based superconductor according to the present invention has a far wider magnetic field region over which superconducting current can flow than does a material containing no titanium, and is a superior superconductor material in this respect as well.

The data for the upper critical field Hc2 given in FIG. 7 was measured from a magnetization M-H curve at different temperatures for a material in which y=0.1, but the data for Hc2 measured for samples in which y=0, 0.05, and 0.2 was almost the same as that of the sample in which y=0.1.

INDUSTRIAL APPLICABILITY

As described above, according to the novel manufacturing method of the present invention, a dense MgB2-based superconductor that exhibits high critical current density, which could only be obtained in the past by sintering in a high-pressure atmosphere, can be manufactured in a low-pressure atmosphere as low as atmospheric pressure, so superconductor wire materials, superconductor bulk materials, and so on for application to electric power cables, magnets, motors, generators, and so forth can be mass produced at a low cost. Therefore, the present invention is extremely useful industrially in that it can provide high-quality superconductors stably at a low price.

Claims

1. An MgB2-based superconductor with high critical current density, wherein either titanium or a titanium compound or both thereof is dispersed in an MgB2-based sintered body and the amounts of magnesium, boron, and titanium contained in the sintered body are expressed as an atomic ratio of Mg:B:Ti of x:2:y, with 0.7x<1.2 and 0.05<y<0.3.

2. The MgB2-based superconductor with high critical current density according to claim 1, wherein either the titanium or the titanium compound or both thereof is present at the MgB2 crystal grain boundary.

3. The MgB2-based superconductor with high critical current density according to claim 1, wherein x and y are such that 0.7<x<1.2 and 0.07<y<0.2.

4. The MgB2-based superconductor with high critical current density according to claim 1, wherein the superconductor has a critical current density of at least 5×105 A/cm2 at a temperature of 20K and in a self field.

5. The MgB2-based superconductor with high critical current density according to claim 1, wherein the superconductor has a critical current density of at least 2×105 A/cm2 at a temperature of 20K and in a magnetic field of 1 T.

6. A method for manufacturing the MgB2-based superconductor with high critical current density according to claim 1, the method comprising compacting a mixture of magnesium, boron, and titanium and sintering the pressed mixture.

7. A method for manufacturing the MgB2-based superconductor with high critical current density according to claim 1, the method comprising forming a mixture of magnesium, boron, and titanium into a wire and firing the wire.

8. A method for manufacturing the MgB2-based superconductor with high critical current density according to claim 1, the method comprising sintering a mixture of magnesium, boron, and titanium, pulverizing the sintered mixture to powder, forming the sintered powder into a wire and firing the wire.

9. The method for manufacturing the MgB2-based superconductor with high critical current density according to claim 6, wherein the sintering is performed under an atmospheric pressure.

10. The method for manufacturing the MgB2-based superconductor with high critical current density according to claim 6, wherein the sintering is performed at a temperature of at least 600° C.

11. The MgB2-based superconductor with high critical current density according to claim 1, wherein x is 0.9 and y is 0.1.

12. The MgB2-based superconductor with high critical current density according to claim 1, wherein x is 0.8 and y is 0.2.

Referenced Cited
U.S. Patent Documents
6586370 July 1, 2003 Holcomb
6687975 February 10, 2004 Tomsic
Foreign Patent Documents
1394112 March 2004 EP
WO 02/069353 September 2002 WO
Other references
  • Zhao et al. “Doping effect of Zr and Ti on the critical current desnity of MgB2 bulk superconductors prepared under ambient pressure”, Physica C 378-38, Oct. 2002, pp. 122-126.
  • Cheng et al. “Chemical doping effect on the crystal structure and superconductivity of MgB2”, Physica C 386, 2003, pp. 588-592.
  • Fu et al. “Microstructures and superconducting properties in Ti-doped MgB2/Ta/Cu tape”, Physica C 386, 2003, pp. 659-662.
  • Anderson, Jr. et al., “Titanium additives to MgB2 conductors”, Physica C 390, 2003, pp. 11-15.
  • Superconducting properties of MgB2 bulk materials prepared by high-pressure sintering, by Y. Takano et al, Applied Physics Letters, vol. 78, No. 19, May 2001, pp. 2914-2916.
  • High critical current density of MgB2 bulk superconductor doped with Ti and sintered at ambient pressure, by Y. Zhao et al, Applied Physics Letters, vol. 79, No. 8, Aug. 2001, pp. 1154-1156.
  • Enhancement of critical current density in MgB2 bulk superconductor by Ti doping, by Y. Zhao et al, Europhysics Letters, vol. 57, No. 3, Feb. 2002, pp. 437-443.
  • Improved chemical stability of Ti-doped MgB2 in water, by Y. Zhao et al, Applied Physics Letters, vol. 80, No. 13, Apr. 2002, pp. 2311-2313.
  • Nanoparticle structure of MgB2 with ultrathin TiB2 grain boundaries, by Y. Zhao et al, Applied Physics Letters, vol. 80, No. 9, Mar. 2002, pp. 1640-1642.
Patent History
Patent number: 6953770
Type: Grant
Filed: May 10, 2002
Date of Patent: Oct 11, 2005
Patent Publication Number: 20040092403
Assignee: International Superconductivity Technology Center, The Juridical Foundation (Tokyo)
Inventors: Yong Zhao (Urayasu), Yong Feng (Tokyo), Yuan Wu (Urayasu), Takato Machi (Tokyo), Yasunori Fudamoto (Tokyo), Naoki Koshizuka (Narashino), Masato Murakami (Tokyo)
Primary Examiner: Colleen P. Cooke
Attorney: Flynn, Thiel, Boutell & Tanis, P.C.
Application Number: 10/333,770